EP0315177B1 - Sintererzeugnis von hoher Festigkeit und Zähigkeit und Verfahren zu seiner Herstellung - Google Patents

Sintererzeugnis von hoher Festigkeit und Zähigkeit und Verfahren zu seiner Herstellung Download PDF

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EP0315177B1
EP0315177B1 EP88118333A EP88118333A EP0315177B1 EP 0315177 B1 EP0315177 B1 EP 0315177B1 EP 88118333 A EP88118333 A EP 88118333A EP 88118333 A EP88118333 A EP 88118333A EP 0315177 B1 EP0315177 B1 EP 0315177B1
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Prior art keywords
strength
toughness
sinter
maintaining
fibrous shape
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EP88118333A
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English (en)
French (fr)
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EP0315177A1 (de
Inventor
Takemi C/O Ube Kenkyusho Yamamura
Toshihiro C/O Ube Kenkyusho Ishikawa
Makoto C/O Ube Kenkyusho Tamura
Masaki C/O Ube Kenkyusho Shibuya
Kiyohito Okamura
Mitsuhiko Dormitory Of Tohoku University Sato
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Ube Corp
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Ube Industries Ltd
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Priority claimed from JP63026198A external-priority patent/JPH01230473A/ja
Priority claimed from JP63026199A external-priority patent/JPH01230474A/ja
Priority claimed from JP63225197A external-priority patent/JPH0672052B2/ja
Application filed by Ube Industries Ltd filed Critical Ube Industries Ltd
Publication of EP0315177A1 publication Critical patent/EP0315177A1/de
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    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
    • C04B35/565—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide
    • C04B35/575—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide obtained by pressure sintering
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
    • C04B35/565—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/64—Burning or sintering processes
    • C04B35/645—Pressure sintering
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/71—Ceramic products containing macroscopic reinforcing agents
    • C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
    • C04B35/80—Fibres, filaments, whiskers, platelets, or the like

Definitions

  • the present invention relates to a high-strength and high-toughness sinter (ceramic composite material) and a process for producing the same.
  • the high-strength and high-toughness sinter according to the present invention is used mainly for applications such as members of an internal combustion engine, e.g., a piston ring or an auxiliary combustion chamber, and members of a rocket engine, e.g., a nose cone or a nozzle.
  • Ceramics having excellent heat resistance known to the art include, e.g., oxide ceramics such as Al2O3, B4O, MgO, ZrO2, and SiO2, carbide ceramics such as SiC, TiC, WC, and B4C, nitride ceramics such as Si3N4, BN, and AlN, boride ceramics such as TiB2 and ZrB2, and silicide ceramics such as MoSi2, WSi2, and CrSi2. Molded articles of these ceramics have been hitherto prepared at a very high temperature.
  • a sintering assistant has been energetically studied for the purpose of lowering the sintering temperature and the sintering pressure. The sintering assistant serves to improve the sinterability of ceramics and, at the same time, to prevent the sinter particles from growing, so that not only the formation of voids among the particles is prevented but also the grain boundaries are packed at a high density.
  • sintering assistant examples include MgO, NiO, CaO, TiO2, Al2O3, Y2O3, B4C, B, and C.
  • These additives are selected because they can bring about the occurrence of a phase reaction between the base ceramic and the additive so as to promote the sintering of the ceramic having a poor self-sinterability or because the sintering can easily proceed due to the formation of a plasticized liquid phase by the additive at a high temperature.
  • B and C can serve to enhance the sinterability through a lowering in the surface energy of SiC crystals.
  • U.S.P. Nos. 4,336,215 and 4,556,526 each disclosed a process for producing a sinter which comprises heat-sintering a mixture of a polymetallocarbosilane with a ceramic powder after molding or simultaneously with the molding.
  • the polymetallocarbosilane used as a binder of a ceramic powder is converted into an inorganic material when the mixture is heated at a high temperature. Since this inorganic material is a substance having a high melting point, the resultant sinter has relatively high strength even at a high temperature. This is because, as described on col. 6, lines 18 to 31 of the U.S.P. No.
  • the sinter produced in the process described in the above-described patents mainly comprises silicon carbide particles, a solid solution composed of SiC and TiC each produced by thermal decomposition of polytitanocarbosilane, and a grain boundary phase mainly composed of TiC 1-x .
  • a sinter having a deflective strength (bending strength) 1.27 ⁇ 1o8 Pa (13.0 kg/mm2) was produced in Example 7 of the U.S.P. No. 4,336,215 by molding a mixture of a silicon carbide powder with polytitanocarbosilane and sintering the molded material at 1,200°C, and a sinter having a deflective strength (bending strength) 2.45 ⁇ 108 Pa (25.1 kg/mm2) was produced in Example 11 of the same U.S. Patent by preliminarily heating the above-described mixture at 600°C, grinding the heated mixture, and hot-pressing the ground mixture at 1800°C.
  • An object of the present invention is to provide a process for producing a high-strength and high-toughness sinter which has high mechanical strength and excellent heat resistance at room temperature, hardly brings about a lowering in the strength even at a high temperature, and further has excellent toughness.
  • the above-described object of the present invention can be attained by a high-strength and high-toughness sinter consisting of a crystal agglomerate maintaining a fibrous shape and composed of crystals of SiC and MC 1-x wherein M is Ti and/or Zr and x is a number of 0 or more but less than 1 (hereinafter referred to as the "first ceramic sinter").
  • the present invention also provides a preferable process for producing the above-described first ceramic sinter, more specifically a process for producing a high-strength and high-toughness sinter consisting of a crystal agglomerate maintaining a fibrous shape and composed of crystals of SiC and MC 1-x wherein M is Ti and/or Zr and x is a number of 0 or more but less than 1, said process comprises forming a laminate consisting of an inorganic fiber composed of the following inorganic material (i), (ii), or (iii) molding the laminate into a predetermined shape, and conducting heat-sintering simultaneously with the molding or after the molding in an atmosphere comprising at least one member selected from the group consisting of a vacuum, an inert gas, a reducing gas, and a hydrocarbon gas at a temperature or 1,700 to 2,200°C:
  • the sinter of the present invention has high mechanical strength and excellent heat resistance at room temperature, hardly brings about a lowering in the strength even at a high temperature and further has excellent toughness, and the process of the present invention enables the above-described sinter to be produced on an industrial scale.
  • the crystal agglomerate maintaining a fibrous shape and constituting the first ceramic sinter of the present invention comprises at least one member selected from among massive, flaky, and acicular SiC crystals, and crystals in the form of an ultrafine grain composed of SiC and MC 1-x , wherein M is Ti and/or Zr and x is a number of 0 or more but less than 1.
  • the term "massive” used herein is intended to mean preferably a mass having a side length of 1 to 20 ⁇ m in which grains are grown in the three-dimensional direction
  • the term “flaky” used herein is intended to mean preferably a scale having a length of 1 to 20 ⁇ m
  • the term “acicular” used herein is intended to mean preferably a shape having a length of 1 to 20 ⁇ m and a length to thickness ratio of 1.5 to 20.
  • the size of the above-described ultrafine particle crystal is usually 5 ⁇ 10 ⁇ 8 m (500 ⁇ ) or less.
  • the first ceramic sinter of the present invention contains 40% by weight of massive, flaky, or acicular SiC crystals. When the amount of these crystals is too small, the strength of the sinter is lowered. The upper limit of the amount of these crystals is usually 95% by weight.
  • the inorganic fiber comprising the above-described inorganic material (i), (ii), or (iii) (hereinafter referred to as the "inorganic fiber [A]") used as the starting material in the process for producing the first ceramic sinter of the present invention exhibits high self-sinterability, which makes it possible to produce an excellent sinter through a treatment at 1,700 to 2,200°C without addition of any sintering assistant.
  • the inorganic fiber [A] can be prepared by a process described in U.S.P. Nos. 4,342,712, 4,515,742 or the like.
  • said inorganic fiber [A] can be prepared by melt-spinning polytitanocarbosilane or polyzirconocarbosilane, making the resultant fiber infusible through a heat treatment in the air, and baking the fiber in an inert gas at 800 to 1,500°C.
  • the above-described inorganic fiber may be used in the fob of a continuous fiber, a chopped short fiber prepared by cutting a continuous fiber, a weave such as a plain weave, a three-dimensional weave, or a non-woven fabric prepared from a continuous fiber, and a sheet material prepared by drawing and arranging a continuous fiber in one direction.
  • crystals are preferentially grown within' an inorganic fiber, so that it becomes possible to produce a ceramic sinter which exhibits a crystal orientation reflecting the form of use of the fiber and has been deformed so as to fill up the gaps between the fibers most effectively.
  • the use of the above-described plain weave as the inorganic fiber brings about the formation of a sinter wherein a crystal agglomerate maintaining a fibrous shape is in the same oriented state as that of the plain weave laminate
  • the use of the above-described sheet material as the inorganic fiber brings about a sinter wherein a crystal agglomerate maintaining a fibrous shape is in the same oriented state as that of a sheet material laminate drawn in one direction
  • the use of the above-described three-dimensional weave as the inorganic fiber brings about a sinter wherein a crystal agglomerate maintaining a fibrous shape is in the same oriented state as that of the three-dimensional weave
  • the use of the above-described chopped short fiber as the inorganic fiber brings about the formation of a sinter wherein a crystal agglomerate maintaining a fibrous shape is oriented at random.
  • the above-described sinters are each prepared in such a state that the section of the crystal agglomerate maintaining a fibrous shape is deformed to have a polygonal shape and the crystal agglomerates are excellently linked or bonded to each other without the intervention of any matrix among them.
  • the ceramic sinter having excellent performance can be produced by preparing an inorganic fiber laminate and conducting heat-sintering after molding of the laminate into a desired shape or simultaneously with the molding.
  • the sintering can be conducted by a process wherein a laminate after molding is sintered under enhanced, atmospheric or reduced pressure or a hot press process wherein molding and sintering are simultaneously conducted.
  • molding is conducted by pressing the laminate under a pressure of 9.81 ⁇ 1010 to 4.9 ⁇ 1012 Pa (100 to 5,000 kg/cm2) through a mold press process, a rubber press process, an extrusion process, or a sheet process to have a predetermined shape.
  • a starting material of the inorganic fiber i.e., polycarbosilane or polytitanocarbosilane, polyzirconocarbosilane, or a commercially available organic polymer may be used as a binder.
  • the molding prepared above is then sintered to give a ceramic sinter of the present invention.
  • a mold made of graphite and sprayed with a releasing agent composed of BN is used, and the laminate is pressed under a pressure of 1.96 ⁇ 109 to 1.96 ⁇ 1012 Pa (2 to 2,000 kg/cm2) with heating, thereby giving a sinter.
  • the heat-sintering temperature is 1,700 to 2,200°C, preferably 1,900 to 2,100°C.
  • the heating at this temperature brings about the formation of massive, flaky, and/or acicular SiC crystals, thus forming a high-strength and high-toughness ceramic sinter wherein the SiC crystals are uniformly dispersed in an ultrafine grain agglomerate comprising SiC and TiC and/or ZrC.
  • the heat-sintering temperature is below 1,700°C, no massive, flaky, or acicular SiC crystal is formed, which makes it impossible to produce a high-strength sinter.
  • the heat-sintering temperature is above 2,200°C
  • the formed SiC crystals are apt to be decomposed.
  • the heat-sintering is conducted in an atmosphere comprising at least one member selected from the group consisting of a vacuum, an inert gas, a reducing gas, and a hydrocarbon gas.
  • the inert gas include nitrogen and carbon dioxide gases
  • examples of the reducing gas include hydrogen and carbon monooxide gases
  • examples of the hydrocarbon gas include methane, ethane, propane, and butane gases.
  • the first ceramic sinter of the present invention exhibits much higher strength at room temperature than that of conventional ceramic sinters, hardly brings about a lowering in the strength even at a high temperature, and exhibits a fracture toughness value 2 to 10 times higher than that of the conventional ceramic sinters.
  • the oxygen and at least part of carbon in a non-stoichiometric amount contained in the inorganic fiber are released during the above-described sintering according to the following reaction: 2C + SiO ⁇ SiC + CO 3C + SiO2 ⁇ SiC + 2CO. Presumably this brings about a lowering in the surface energy of the SiC grain and thus improves the sinterability.
  • the sinter may contain 10% by weight, based on the sinter, of free carbon in a non-stoichiometric amount with respect to the silicon atom and M and further 15% by weight, based on the sinter, of oxygen in the form of SiO y , wherein 0 ⁇ y ⁇ 2, and/or MO z , wherein 0 ⁇ z ⁇ 2.
  • the sinter may be produced also by, if necessary, impregnating the above-described molding of the laminate before sintering with a starting material of the inorganic fiber, i.e., polycarbosilane or polytitanocarbosilane, polyzirconocarbosilane, or a silane coupling agent to treat the surface of the inorganic fiber constituting the above-described laminate, preliminarily heating the treated laminate at 800 to 1,500°C in an atmosphere comprising at least one member selected from the group consisting of a vacuum, an inert gas, a reducing gas, and a hydrocarbon gas, and sintering the heated laminate at 1,700 to 2,200°C.
  • a starting material of the inorganic fiber i.e., polycarbosilane or polytitanocarbosilane, polyzirconocarbosilane, or a silane coupling agent to treat the surface of the inorganic fiber constituting the above-
  • a 5-l three-necked flask was charged with 2.5 l of anhydrous xylene and 400 g of sodium.
  • the mixture was heated to the boiling point of xylene under a nitrogen gas stream, and 1 l of dimethyldichlorosilane was dropwise added thereto over a period of 1 hr. After the completion of addition, the mixture was heated under reflux for 10 hr to form precipitates.
  • the precipitates were collected by filtration and washed with methanol and then with water to prepare 420 g of polydimethylsilane in the form of a white powder.
  • Polytitanocarbosilane prepared in Reference Example 2 which is a starting material of the inorganic fiber [A] was melt-spun into a fiber.
  • the fiber was heated in the air to 180°C at a temperature raising rate of 20°C/hr to make the fiber insufible, heated in a nitrogen atmosphere to 1300°C at a temperature raising rate of 200°C/hr, and maintained at that temperature for 1 hr.
  • the heat-treated fiber was allowed to cool to prepare the inorganic fiber [A].
  • the inorganic fiber [A] was ground in a mortar made of silicon nitride to prepare the powder [A] of 74 ⁇ m (200 mesh) or less.
  • Polytitanocarbosilane prepared in Rerefence Example 2 was melt-spun into a fiber.
  • the fiber was heated in the air to 170°C at a temperature raising rate of 20°C/hr to make the fiber infusible, heated in a nitrogen atmosphere to 1000°C at a temperature raising rate of 200°C/hr, and maintained at that temperature for 1 hr.
  • the heat-treated fiber was allowed to cool to prepare an inorganic continuous fiber [A].
  • Plain woven fabrics each comprising the above-described inorganic continuous fiber [A] were put on top of each other.
  • the laminate was set in a carbon die (a sheet material having a size of 3 mm x 10 mm x 10 mm), hot-pressed in an argon gas stream under a pressure of 600 kg/cm2 at 2,000°C for 0.5 hr to produce the first ceramic sinter of the present invention.
  • the ceramic sinter of the present invention thus produced had a bending strength of 7.85 ⁇ 108 Pa (80 kg/mm2) (at room temperature) and 7.45 ⁇ 108 Pa (76 kg/mm2) (at 1400°C) and a density of 3.0 g/cm3. Further, the ceramic sinter exhibited a fracture toughness value (Kic: 24) 8 times higher than that of a ceramic sinter produced from only the powder without use of the plain woven fabric.

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  • Ceramic Engineering (AREA)
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  • Materials Engineering (AREA)
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Claims (14)

  1. Sintererzeugnis von hoher Festigkeit und Zähigkeit, bestehend aus einem eine faserige Gestalt beibehaltenden Kristallagglomerat und zusammengesetzt aus SiC- und MC1-x-Kristallen wobei M Ti und/oder Zr ist und x eine Zahl von 0 oder mehr, jedoch weniger als 1.
  2. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 1, wobei diese eine faserige Gestalt beibehaltende Kristallagglomerate massive, flockenartige und/oder nadelförmige SiC-Kristalle und ultrafeine SiC- und MC1-x-Kornkristalle umfassen, wobei M Ti und/oder Zr ist und x eine Zahl von 0 oder mehr, jedoch weniger als 1.
  3. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 1, wobei diese eine faserige Gestalt beibehaltenden Kristallagglomerate sich in einem solchen deformierten Zustand befinden, um eine möglichst effiziente Auffüllung der Faserzwischenräume zu ermöglichen.
  4. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 3, wobei die Bereiche wenigstens eines Teils der Fasern der eine faserige Gestalt beibehaltenden Kristallagglomerate in eine polygonale Form deformiert sind.
  5. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 1, wobei diese eine faserige Gestalt beibehaltenden Kristallagglomerate ohne das Eingreifen einer Matrix ausgezeichnet miteinander verbunden oder verkettet sind.
  6. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 5, wobei dieses eine faserige Gestalt beibehaltende Kristallagglomerat sich in dem gleichen orientierten Zustand befindet wie der eines einfachen gewebten Laminats.
  7. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 5, wobei dieses eine faserige Gestalt beibehaltende Kristallagglomerat den gleichen orientierten Zustand aufweist wie der eines Laminats, eines Bandmaterials, welches in eine Richtung gezogen und angeordnet wird.
  8. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 1, wobei dieses eine faserige Gestalt beibehaltende Kristallagglomerat sich in dem gleichen orientierten Zustand befindet wie eine dreidimensional gewebtes Erzeugnis.
  9. Sintererzeugnis von hoher Festigkeit und Zähigkeit nach Anspruch 1, dadurch gekennzeichnet, daß dieses eine faserige Gestalt beibehaltende Kristallagglomerat zufällig orientiert ist.
  10. Verfahren zur Herstellung eines Sintererzeugnisses mit hoher Festigkeit und Zähigkeit, bestehend aus einem eine faserige Gestalt beibehaltenden Kristallagglomerat und zusammengesetzt aus SiC- und MC1-x-Kristallen, wobei M Ti und/oder Zr ist und x eine Zahl von 0 oder mehr, jedoch weniger als 1, das Verfahren umfaßt das Bilden eines Laminats, bestehend aus einer anorganischen Faser, zusammengesetzt aus dem folgenden anorganischen Material (i), (ii) oder (iii), Formen des Laminats in eine vorherbestimmte Form und Durchführen einer Wärmesinterung, gleichzeitig mit dem Formen oder nach dem Formen in einer Atmosphäre, welche wenigstens ein Bestandteil enthält, ausgewählt aus der Gruppe, bestehend aus einem Vakuum, einem Edelgas, einem reduzierenden Gas und einem Kohlenwasserstoffgas bei einer Temperatur von 1700 bis 2200 °C:
    (i) eine amorphe Substanz, im wesentlichen bestehend aus Silicium, M, Kohlenstoff und Sauerstoff,
    (ii) ein Agglomerat, umfassend feine kristalline Körner mit einem Durchmesser von 50 µm (500 Å) oder weniger und im wesentlichen bestehend aus β-SiC, MC, einer festen Lösung, zusammengesetzt aus β-SiC und MC und/oder MC1-x, wobei SiOy und MOz, O < y, z ≦ 2, um diese ultrafeinen, kristallinen Körner vorhanden sein können, und
    (iii) ein System, umfassend eine Mischung aus dieser amorphen Substanz (i) und diesem Agglomerat (ii).
  11. Verfahren zur Herstellung eines Sintererzeugnisses mit hoher Festigkeit und Zähigkeit nach Anspruch 10, wobei diese anorganische Faser eine zerhackte, kurze Faser ist.
  12. Verfahren zur Herstellung eines Sintererzeugnisses mit hoher Festigkeit und Zähigkeit nach Anspruch 10, wobei diese inorganische Faser zu einem einfachen Gewebe verwoben ist.
  13. Verfahren zur Herstellung eines Sintererzeugnisses mit hoher Festigkeit und Zähigkeit nach Anspruch 10, wobei diese inorganische Faser ein Bandmaterial ist, welches in eine Richtung gezogen und angeordnet ist.
  14. Verfahren zur Herstellung eines Sintererzeugnisses mit hoher Festigkeit und Zähigkeit nach Anspruch 10, wobei diese inorganische Faser in Form eines nicht gewobenen Erzeugnisses oder eines dreidimensionalen Gewebes vorliegt.
EP88118333A 1987-11-05 1988-11-03 Sintererzeugnis von hoher Festigkeit und Zähigkeit und Verfahren zu seiner Herstellung Expired - Lifetime EP0315177B1 (de)

Applications Claiming Priority (10)

Application Number Priority Date Filing Date Title
JP27988487 1987-11-05
JP27988587 1987-11-05
JP279884/87 1987-11-05
JP279885/87 1987-11-05
JP63026198A JPH01230473A (ja) 1987-11-05 1988-02-05 高強度セラミック複合材料およびその製造方法
JP26198/88 1988-02-05
JP26199/88 1988-02-05
JP63026199A JPH01230474A (ja) 1987-11-05 1988-02-05 高強度セラミック成形体の製造方法
JP63225197A JPH0672052B2 (ja) 1988-09-08 1988-09-08 高強度・高靱性焼結体およびその製造方法
JP225197/88 1988-09-08

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US5049329A (en) * 1989-10-30 1991-09-17 Corning Incorporated Process for forming ceramic matrix composites
DE4102315A1 (de) * 1991-01-26 1992-07-30 Solvay Deutschland Heteroelement enthaltende polycarbosilane
JP2579854B2 (ja) * 1991-08-14 1997-02-12 宇部興産株式会社 無機繊維焼結体及びその製造方法
GB2259299B (en) * 1991-08-14 1996-01-10 Ube Industries Inorganic fiber sinter and process for producing same

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US4342712A (en) * 1979-06-28 1982-08-03 Ube Industries, Ltd. Process for producing continuous inorganic fibers
JPS60226462A (ja) * 1984-04-24 1985-11-11 宇部興産株式会社 無機繊維強化耐熱セラミツク複合材料
JPS61111974A (ja) * 1984-11-06 1986-05-30 宇部興産株式会社 無機繊維強化耐熱セラミツク複合材料

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DE3883155T2 (de) 1993-12-02

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